Aluminophosphate glass composition

ABSTRACT

The invention relates to aluminophosphate-based glasses suitable for use as a solid laser medium, which further contains SiO 2  and B 2 O 3 . The laser glasses possess desirable figure of merit values for FOM TM  and FOM laser , as described herein.

SUMMARY OF THE INVENTION

The invention relates to aluminophosphate-based glasses suitable for use as a solid laser medium. In particular, the invention relates to improving the physical and laser properties of phosphate-based glass composition that also contain alumina, such as through the addition of certain amounts of silica and/or borate.

Laser glasses are produced by doping host glass systems with rare earth elements that have the ability to lase, such as neodymium and ytterbium. The lasing ability of these rare earth doped laser glasses results from the light amplification achieved by stimulated emission of the excited rare earth element ions within the glass.

Phosphate laser glasses are well known for use as a host matrix for high average power and high peak energy laser systems. For example, U.S. Pat. No. 4,661,284 (Cook et al.) discloses a neodymium-doped silica and/or boron-containing phosphate laser glass that is said to a relatively low self-concentration quenching rate, high thermal shock resistance and high induced emission cross-section compared to previous phosphate laser glasses. These glasses do not contain alumina.

U.S. Pat. No. 4,075,120 (Myers et al.) discloses laser phosphate glass compositions that are said to be suitable for high energy, high peak power laser applications, and described as containing substantial amounts of selected alkaline earth oxides and substantial amounts of selected alkali metal oxides. The glasses are further said to possess high gain, low nonlinear refractive index, good chemical durability and good optical quality. The specific glasses disclosed by U.S. Pat. No. '120 contain relatively high amounts of alkali metals and/or alkaline earth metals, and relatively low amounts of Al₂O₃.

U.S. Pat. No. 5,322,820 (Myers et al.) discloses phosphate glass compositions that are said to provide high average power operation with a balance of athermal performance, high gain, and high rupture strength. The glasses are also said to exhibit good chemical durability. The specific glasses disclosed by U.S. Pat. No. '820 contain relatively high amounts of Al₂O₃ and/or La₂O₃.

U.S. Pat. No. 4,929,387 (Hayden et al.) and U.S. Pat. No. 5,032,315 (Hayden et al.) disclose phosphate glass compositions, containing little or no silica, that are said to be useful in high average power laser while exhibiting high thermal conductivity and low coefficients of thermal expansion. The glasses are also said to exhibit good chemical durability. The specific glasses disclosed by U.S. Pat. No. '387 and U.S. Pat. No. '315 generally contain relatively high amounts of alkali metals and/or alkaline earth metals, in combination with relatively high amounts of Al₂O₃.

U.S. Pat. No. 5,053,165 (Tortani et al.) discloses phosphate-based glass compositions that are said to be suitable for high average power laser application, and characterized by strong thermal shock resistance. The specific glasses disclosed by Tortani et al. contain relatively high amounts of alkali metals and/or alkaline earth metals, and do not contain SiO₂ or B₂O₃.

U.S. Pat. No. 4,820,662 (Izumitani et al.) discloses phosphate glass compositions wherein part of the main component of the phosphate laser glass, P₂O₅, is replaced with SiO₂ to reduce the coefficient of thermal expansion and increase shock resistance. To counteract the deterioration of chemical durability due to the large amounts of SiO₂ in the phosphate, Al₂O₃ can be added to the glass. Also, replacing some of the SiO₂ with Al₂O₃ is said to decrease the stimulated emission cross section. The specific glasses disclosed by Izumitani et al. contain relatively high amounts of alkali metals in combination with relatively high total amounts of SiO₂ and Al₂O₃.

U.S. Pat. No. 6,853,659 (Hayden et al.) discloses a laser system for using highly doped phosphate-based glass compositions. The specific glasses disclosed by U.S. Pat. No. '659 contain relatively high amounts of rare earth metals, and do not contain SiO₂ or B₂O₃. U.S. Pat. No. 6,911,160 (Myer et al.) also discloses highly doped phosphate laser glasses.

U.S. Pat. No. 5,663,972 (Payne et al.) discloses Nd-doped phosphate laser glasses described as having broad emission bandwidths, i.e., greater than about 29 nm. The glass is composed primarily of P₂O₅, Al₂O₃, and MgO.

U.S. Pat. No. 5,526,369 and WO 94/08373 (Hayden et al.) also discloses Nd-doped phosphate laser glasses. In this case, the laser glass is said to desirably have a narrow emission bandwidth (less than 26 nm) to improve extraction efficiency. In this typical type of laser, the emission of the laser is narrow compared to the emission bandwidth, and thus, the emitted light at wavelengths outside of the narrow bandwidth at which the laser operates is effectively wasted. For this reason, narrow emission bandwidths were desirable. The glasses disclosed by U.S. Pat. No. '369 contain relatively high total amounts of alkali metals and alkaline earth metals.

In addition to phosphate glasses, silicates, borates, borosilicates, and aluminates have also been used as host glass matrix systems for lasing ions. Silicate, borate, borosilicates, and aluminate glasses have broader emission bandwidth for Nd lasing ions, in comparison to phosphate glasses.

However, there are disadvantages associate with the use of these glasses. For example, silicate glasses normally melt at very high temperature, unless they contain significant amount of modifiers, such as alkali metals or alkaline earths metals. Borate glasses, on the other hand, have low temperature melting characteristics, but they require substantially high concentrations of alkali metals or alkaline earth metals to be stable in ambient environments. Borosilicate glasses can be durable at ambient temperature and also are melted at temperatures comparable to standard commercial glasses, such as soda-lime glass. However, typical commercial borosilicate glasses contain significant amounts of alkali metals, which promote high borate volatility, similar to phosphate glass, during melting. Aluminate glasses exhibit particularly broad emission bandwidths and are attractive for short pulse laser operation. But, these glasses have a very high tendency towards crystallization.

As mentioned above, U.S. Pat. No. 5,663,972 discloses Nd-doped phosphate laser glasses having broad emission bandwidths that are composed primarily of P₂O₅, Al₂O₃, and MgO. This disclosure resulted in the production of the phosphate glass APG-2, sold by Schott North America, Inc. APG-2 is a laser glass having very desirable thermo-mechanical properties for high power laser use.

Another useful commercial phosphate-based glass having a broad emission bandwidth is the glass APG-1, also sold by Schott North America, Inc. This glass resulted from the disclosure of U.S. Pat. No. 4,929,387 (Hayden et al.) which as described above discloses phosphate glass compositions, containing little or no silica, and containing relatively high amounts of alkali metals and/or alkaline earth metals, in combination with relatively high amounts of Al₂O₃. While APG-2 contains significant amounts of MgO, APG-1, on the other hand, contains significant amounts of alkali metals. APG-1 is a laser glass having very desirable laser properties for high power laser use. Thus, in comparison, while both APG-1 and APG-2 glasses exhibit desirable properties for use in high power lasers, APG-1 exhibits better laser properties, while APG-2 exhibits better thermo-mechanical properties.

Thus, an aspect of the present invention is to provide a phosphate-based glass composition for use as a solid laser medium which, like the commercial glasses APG-1 and APG-2, contains P₂O₅ and Al₂O₃. In the glasses according to the invention a combination of desirable laser properties (such as possessed by APG-1) and desirable thermo-mechanical properties (such as possessed by APG-2) is sought through manipulation of the amounts of SiO₂ and/or B₂O₃.

Upon further study of the specification and appended claims, further aspects and advantages of this invention will become apparent to those skilled in the art.

In accordance with the invention, there is provided an aluminophosphate glass composition containing amounts of a SiO₂ and/or B₂O₃, which exhibits advantageous laser properties and thermo-mechanical properties, and which is suitable for use in a high power laser.

The glasses disclosed herein are suitable for use in large flashlamp pumped laser systems intended to generate mega-Joule levels of energy at repetition rates exceeding 10 Hz. Laser diode pumping is also possible. Such lasers have the potential to drive laser fusion power plants in the future. The glasses disclosed herein are also suitable in smaller lasers where high repetition rate operation is desirable while still having a large output fluence at or near the damage level of the employed optical components in the laser system. Applications of such laser systems include laser shock peening and plasma creation for scientific research or as a source for other radiation. Laser shock peening is a process whereby through use of a powerful laser compressive residual stress is produced in the surface of metals thereby increasing the fatigue life thereof.

In accordance with the invention, the aluminophosphate glass can optionally contain amounts of conventional modifier oxides, such as alkali and/or alkaline earth metals, so long as their inclusion does not result in poor melting behavior and does not compromise the desirable features of the aluminophosphate glass. The total amount of such modifiers is desirable less than about 26 mol % of monovalent modifiers, such as Na₂O, and less than about 25 mol % of divalent modifiers, such as MgO.

According to a further aspect of the invention, the glasses in accordance with the invention are characterized by either: (a) a relatively high amount of alkali metals R₂O (R═Li, Na, K, Rb, Cs) in combination with a relatively low amount of alkaline earth metals MO (M=Mg, Ca, Sr, Ba, Zn); or (b) a relatively high amount of alkaline earth metals MO (M=Mg, Ca, Sr, Ba, Zn) in combination with a relatively low amount of alkali metals R₂O (R═Li, Na, K, Rb, Cs).

In addition, while P₂O₅, Al₂O₃, SiO₂, and B₂O₃, are all network formers, the glasses according to the invention are phosphate-based glasses wherein the P₂O₅ content is greater than the sum of SiO₂, B₂O₃, and Al₂O₃.

Further, in the glasses according to the invention, it is desirable to keep the Al₂O₃ content within a relatively narrow range, particularly when higher amounts of alkali metals R₂O are present.

In accordance with an aspect of the invention, the aluminophosphate glass composition comprises (based on mol %):

SiO₂  0.00-12.00 B₂O₃  0.00-15.00 Al₂O₃  6.00-11.00 P₂O₅ 55.00-67.00 Li₂O  0.50-26.00 K₂O 0.00-4.00 Na₂O 0.00-4.00 Rb₂O 0.00-4.00 Cs₂O 0.00-4.00 MgO  0.00-25.00 ZnO 0.00-6.00 TiO₂ 0.00-6.00 La₂O₃  0.00-10.00 Nd₂O₃ 0.00-6.00 R₂O (R = Li, Na, K, Rb, Cs)  0.50-26.00 MO (M = Mg, Ca, Sr, Ba, Zn)   0.00-25.00. wherein Ln₂O₃ (Ln=Nd, Yb, or other lasing rare earth ions) is >0.00-10.00 mol % (for example, 0.01-10.00 mol % or 0.01-6.00 mol %);

-   -   R₂O is 8.0-26.0 mol % and MO is 0.0-6.0 mol %, or R₂O is 0.5-8.0         mol % and MO is 6.0-25.0 mol %;     -   the sum of SiO₂, B₂O₃, and Al₂O₃ is 6.0-28.0 mol %; and     -   when R₂O is ≧16.0 mol %, then Al₂O₃ is 6.0-10.0 mol % and the         sum of SiO₂, B₂O₃, and Al₂O₃ is 6.0-15.0 mol %.

In accordance with another aspect of the invention, aluminophosphate glass composition comprises (based on mol %):

SiO₂  0.00-12.00 B₂O₃  0.00-15.00 Al₂O₃  6.00-11.00 P₂O₅ 55.00-67.00 Li₂O  0.50-26.00 K₂O 0.00-4.00 Na₂O 0.00-4.00 Rb₂O 0.00-4.00 Cs₂O 0.00-4.00 MgO  0.00-25.00 ZnO 0.00-6.00 TiO₂ 0.00-6.00 La₂O₃  0.00-10.00 Nd₂O₃ 0.00-6.00 R₂O (R = Li, Na, K, Rb, Cs)  0.50-26.00 MO (M = Mg, Ca, Sr, Ba, Zn)   0.00-25.00. wherein Ln₂O₃ (Ln=Nd, Yb, or other lasing rare earth ions) is >0.00-10.00 mol % (for example, 0.01-10.00 or 0.01-6.00 mol %);

-   -   R₂O is 8.0-26.0 mol % and MO is 0.0-6.0 mol %, or R₂O is 0.5-8.0         mol % and MO is 6.0-25.0 mol %;     -   the sum of SiO₂ and B₂O₃ is 3-20 mol %, and the sum of SiO₂,         B₂O₃, and Al₂O₃ is 6.0-28.0 mol %; and     -   when R₂O is ≧16.0 mol %, then Al₂O₃ is 6.0-10.0 mol % and the         sum of SiO₂, B₂O₃, and Al₂O₃ is 6.0-15.0 mol %.

In accordance with another aspect of the invention, there is provided a glass composition comprising:

10.00 mol % S_(i)O₂ (±2.00 mol %), 8.00 mol % B₂O₃ (±2.00 mol %), 8.80 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 10.80 mol % Li₂O (±2.00 mol %), <1.0 mol % MgO, <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).

In accordance with another aspect of the invention, there is provided a glass composition comprising:

8.50 mol % S_(i)O₂ (±2.00 mol %), 5.00 mol % B₂O₃ (±2.00 mol %), 10.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 12.00 mol % Li₂O (±2.00 mol %), <1.0 mol % MgO, <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).

In accordance with another aspect of the invention, there is provided a glass composition comprising:

7.00 mol % S_(i)O₂ (±2.00 mol %), 7.00 mol % B₂O₃ (±2.00 mol %), 8.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 10.00 mol % Li₂O (±2.00 mol %), 5.00 mol % MgO (±1.00 mol %), <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).

In accordance with another aspect of the invention, there is provided a glass composition comprising:

4.00 mol % S_(i)O₂ (±2.00 mol %), 5.00 mol % B₂O₃ (±2.00 mol %), 9.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 1.50 mol % Li₂O (±2.00 mol %), 15.00 mol % MgO (±2.00 mol %), <1.0 mol % La₂O₃, 0.2-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).

In accordance with another aspect of the invention, there is provided a glass composition comprising:

<3.0 mol % S_(i)O₂, 7.00 mol % B₂O₃ (±2.00 mol %), 10.00 mol % Al₂O₃ (±1.00 mol %), 60.00 mol % P₂O₅ (±3.50 mol %), 1.50 mol % Li₂O (±2.00 mol %), 15.00 mol % MgO (A: 2.00 mol 5.00 mol % ZnO (±1.00 mol %), <1.0 mol % La₂O₃, 0.3-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).

According to a further aspect of the invention, the glass composition contains 7-26 mol % Li₂O, the sum of SiO₂ and B₂O₃ is 3-20 mol %, and the sum of SiO₂, B₂O₃, and Al₂O₃ is 10.0-28.0 mol %.

According to a further aspect of the invention, the glass composition contains 14-25 mol % MgO, the sum of SiO₂ and B₂O₃ is 3-12 mol %, and the sum of SiO₂, B₂O₃, and Al₂O₃ is 10.0-25.0 mol %.

According to a further aspect of the invention, the glass composition contains 8.0-26.0 mol % R₂O and 0.0-6.0 mol % MO. According to a further aspect of the invention, the glass composition contains 0.5-3.0 mol % R₂O and 10.0-25.0 mol % MO.

With respect to the laser glass application, the aluminophosphate glass composition according to the invention contains a sufficient amount of Ln₂O₃, wherein Ln represents a rare earth lasing ion, to provide lasing capabilities. Generally, the amount of Ln₂O₃ is about 0.3-10.0 mol %, for example, 0.5-8.0 mol % or 0.3-6.0 mol % or 0.5-5.0 mol %. The lasing element Ln is preferably Nd, but can also be Yb, and even, for example, Er or Pr. Yb and Nd both lase in the IR range. Er has a lasing wavelength that is eyesafe, and Pr can lase at visible wavelengths. Still other lasing ions are Sm, Eu, Tb, Dy, Ho and Tm. The lasing ions can be used alone or in combinations of two or more elements.

These glass compositions employ P₂O₅ as the principle glass network former. The level of P₂O₅ is preferably maximized. Generally, the P₂O₅ content is 55-67, preferably 57-65, especially 59-62 mole %. The P₂O₅ content can also be, for example, 55.0, 56.0, 56.5, 57.0, 58.0, 58.5, 59.0, 60.0, 60.5, 61.0, 62.0, 62.5, 63.9, 64.0, 65.0, 66.0, etc., mole %.

Al₂O₃, La₂O₃, SiO₂ and B₂O₃ all act as network formers, and tend to enhance the chemical durability of the glass, and reduce water solubility. SiO₂ and B₂O₃ each act as primary network formers, in addition to P₂O₅. Al₂O₃ and La₂O₃ act as intermediate glass formers.

Amounts of SiO₂ can also increase thermal conductivity. However, large amounts of SiO₂ may increase the crystallization tendency and/or lead to phase separation, and may reduce emission cross section. The amount of SiO₂ used in preparing the glass is 0.0-12.0 mol %, such as 3.0-10.0 mol %, for example, 0.5, 1.0, 2.0, 3.0, 4.0, 5.0, 6.0, 7.0, 8.0, 9.0, 10.0, or 11.0 mol %.

B₂O₃ can also increase thermal conductivity. But, high amounts of B₂O₃ can adversely impact the thermal expansion and thereby reduce FOM_(TM). The amount of B₂O₃ used in preparing the glass is 0.0-15.00, for example, 0.0-9.0 mol %, such as 3.0-9.0 mol %, for example, 0.5, 1.0, 2.0, 3.0, 4.0, 5.0, 6.0, 7.0, 8.0, 9.0, 10.0, 11.0, 12.0, 13.0, and 14.0 mol %.

As noted, Al₂O₃ and La₂O₃ act as intermediate glass formers. As a result, Al₂O₃ and La₂O₃ each exhibit characteristics of both a glass former and a glass modifier. Al₂O₃ can provide not only better chemical durability, but also better thermomechanical properties. However, high amounts of Al₂O₃ may induce crystallization, and reduce emission cross section and thermal expansion coefficient. The level of Al₂O₃ is generally 6.0 to 11.0%, such as 6.0-10.0%, or 6.5-10.5%. Other levels of Al₂O₃ are, for example, 7.0, 7.5, 7.8, 8.0, 8.5., 9.0, 9.5, 10.0, 10.5 mole %. The amount of La₂O₃ used in preparing the glass is 0.0-10.0%, such as 1.0-7.0 mol %, for example, 0.2, 0.5, 1.0, 2.0, 3.0, 4.0, 5.0, 6.0, 7.0, 8.0, or 9.0 mol %.

The alkaline earth metals, MO, enhance the chemical durability properties of the glass. In general, the amount of MO is up to 25.0 mol %. The preferred alkaline earth metal is MgO, since amounts of MgO tend to provide higher FOM_(TM). Low amounts of ZnO can be beneficial with respect to FOM_(TM). Preferably, the amount of MgO in the glass is up to 25.0 mol % (e.g., 14/0 to 24.0 mol %), the amount of ZnO is 0.0-6.0 mol %, the amounts of CaO, SrO, and BaO are each 0.0-5.0 mol %, especially 0.0-2.5 mol %, and in particular 0.0-1.0 mol %, and the total combined amount of CaO, SrO, and BaO is 0.0-5.0 mol %, especially 0.0-2.5 mol %, and in particular 0.0-1.0 mol %.

The alkali metals content, R₂O, will impact certain properties of the glass such as linear thermal expansion coefficient and emission cross section. In general, the amount of R₂O is 0.50-26.00 mol %. The preferred alkali metal is Li₂O, since amounts of Li₂O tend to provide higher FOM_(TM). Preferably, the amount of Li₂O in the glass is 0.50-26.00 mol %, preferably e.g., 7 to 26 mol %, the amounts of Na₂O, K₂O, Rb₂O, and Cs₂O are each 0.0-4.0 mol %, especially 0.0-2.0 mol %, and in particular 0.0-1.0 mol %, and the total combined amount of Na₂O, K₂O, Rb₂O, and Cs₂O is 0.0-4.0 mol %, especially 0.0-2.0 mol %, and in particular 0.0-1.0 mol %, such as 0.0-0.5 mol %.

According to a further aspect of the invention, the alkaline earth metals content, MO, is 0.0-6.0 mol %, especially 0.0-3.0 mol %, and the alkali metals content, R₂O, is 8.0-26.0 mol %, especially 10.0-25.0 mol %. In this case, the alkaline metal is preferably MgO, the amount of ZnO is 0.0-6.0 mol %, and the total combined amount of CaO, SrO, and BaO is 0.0-5.0 mol %, especially 0.0-2.5 mol %, and in particular 0.0-1.0 mol %. Also, in this case, the alkali metal is preferably Li₂O, and the total combined amount of Na₂O, K₂O, Rb₂O, and Cs₂O is 0.0-4.0 mol %, especially 0.0-2.0 mol %, and in particular 0.0-1.0 mol %, such as 0.0-0.5 mol %.

According to another aspect of the invention, the alkaline earth metals content, MO, is 6.0-25.0 mol %, especially 14.0-24.0 mol %, and the alkali metals content, R₂O, is 0.5-8.0 mol %, especially 0.5-3.0 mol %. In this case, the alkaline metal is preferably MgO, the amount of ZnO is 0.0-6.0 mol %, and the total combined amount of CaO, SrO, and BaO is 0.0-5.0 mol %, especially 0.0-2.5 mol %, and in particular 0.0-1.0 mol %. Also, in this case, the alkali metal is preferably Li₂O, and the total combined amount of Na₂O, K₂O, Rb₂O, and Cs₂O is 0.0-4.0 mol %, especially 0.0-2.0 mol %, and in particular 0.0-1.0 mol %, such as 0.0-0.5 mol %.

As noted above, Yb₂O₃ and/or Nd₂O₃ provide the preferred lasing ions for the glass composition. Alternatively, other rare earths or combinations of rare earth oxides can be used as lasing ions, for example Er₂O₃ and/or Pr₂O₃. In addition, as is well known to those skilled in the art, these laser glasses can be doped with small amounts of transition metals, such as Cr₂O₃, or other rare earth ions, such as Yb₂O₃ and CeO₂, that act as sensitizers to the primary lasing ion(s). For example, Cr₂O₃ can function as a sensitizer for Yb, and CeO₂, Cr₂O₃ and Yb₂O₃ can function as sensitizers for Er. For Cr₂O₃ the amount of sensitizer is, for example, >0.00 to 0.40 wt %, preferably 0.01 to 0.20 wt %, and for Yb₂O₃ the amount of sensitizer is, for example, >0.00 to the solubility limit for Yb₂O₃ in the glass, preferably 5 wt % to 25 wt %.

In addition to the laser application, glasses according to the invention prepared without a lasing ion can also be used as a cladding glass in a laser waveguide device. Additionally, by doping the glasses according to the invention with one or more transition metals that introduce absorption at the lasing wavelength, the resultant transition metal-doped glass can serve as an edge cladding glass in certain laser system designs.

With regards to the additional components, the glass contains a maximum of 4 wt %, especially a maximum of 2 wt %, of conventional additives or impurities, such as refining agents (e.g., As₂O₃ and Sb₂O₃) and antisolarants (e.g., Nb₂O₅). The glass can contain small amounts of TiO₂ as an antisolarant. However, as the presence of TiO₂ can lead to undesirable discoloration of the glass. Therefore, the amount of TiO₂ is preferably 0.0-1.0 mol %, especially 0-0.5 mol %.

In addition, the glass composition may contain halides to help dry the melt or residual water and to help refining of the glass. For example, the glass composition may contain up to 9 wt % F, preferably not more 5 wt %, and, up to 5 wt % Cl, although Cl is less preferred than F.

To be useful for the generation of high average power, phosphate-based laser glass should possess advantageous thermal-mechanical properties. During operation, cooling of the exterior surfaces of the solid laser material will result in the formation of a thermal gradient wherein the internal temperature of the material is higher than the temperature of the external surfaces. This thermal gradient can then lead to a stress gradient within the solid laser material which can eventually result in fracture of the active solid laser material.

In general, the thermal-mechanical properties of lasers are assessed by a parameter called the thermal-mechanical figure of merit, FOM_(TM). The thermal mechanical figure of merit is proportional to the maximum thermal gradient that the material can tolerate without fracture, and also reflects the magnitude of the thermal gradient for a given situation.

The thermal-mechanical figure of merit, FOM_(TM), is calculated by the following formula:

FOM_(TM) =K _(90C) K _(IC)(1−ν)/(αE)

wherein

K_(90C) is the Thermal Conductivity measured at 90° C. [W/mK],

K_(IC) is the Indentation Fracture Toughness,

ν is Poisson's ratio,

E is Young's modulus [GPa]; and

α is the Linear Coefficient of Thermal Expansion, over 20-300° C. [10⁻⁷/K].

The Indentation Fracture Toughness can be determined at a 3.0N Load or a 9.8N Load, whichever is needed to make the measurement. To make the measurement, a load is applied that will yield tiny cracks in the glass. Glasses needing the larger load 9.8N load to yield cracks are more attractive.

Thus, as can be seen from the above equation, to increase the FOM_(TM) it is desirable to have a high thermal conductivity and low the coefficient of thermal expansion, Poisson's ratio, and Young's modulus. For a given thermal gradient, the amount of stress in the glass part is reduced as the product of thermal expansion and Young's modulus is lower, Higher values of thermal conductivity help to reduce the magnitude of the thermal gradient that results for a given amount of heat deposited into the glass.

Laser properties can be measured in accordance with the Judd-Ofelt theory, the Fuchtbauer-Ladenburg theory, or the McCumber method. A discussion of the Judd-Ofelt theory and the Fuchtbauer-Ladenburg theory can be found in E. Desurvire, Erbium Doped Fiber Amplifiers, John Wiley and Sons (1994), The McCumber method is as discussed in, for example, Miniscalco and Quimby, Optics Letters 16(4) pp 258-266 (1991). See also Kassab, Journal of Non-Crystalline Solids 348 (2004) 103-107. The Judd-Ofelt theory and the Fuchtbauer-Ladenburg theory evaluate laser properties from an emission curve, whereas the McCumber method uses the absorption curve of the glass.

Regarding emission bandwidth, if one has a measured emission curve (such as collected in a Judd-Ofelt or Fuchtbauer-Ladenburg analysis) or a calculated emission curve (from a McCumber analysis) one can get emission bandwidth in two ways. The first way is to simply measure the width at half of the maximum value (called emission bandwidth full width half maximum or Δλ_(FWHM)).

For glasses using Yb as the lasing ion, an emission curve for Yb will exhibit a narrow feature at ˜980 nm. If this feature is prominent, the Δλ_(FWHM) value will only reflect the width of this one feature and the rest of the curve will not contribute. As a result the Δλ_(FWHM) value is not always a reliable indicator of the emission bandwidth for Yb.

The second method divides every point on the emission curve by the total area under the curve. The result, called a linewidth function, will have a peak value that is defined as the inverse of the effective bandwidth, Δλ_(eff). By this method the entire emission curve always contributed to the emission bandwidth result. It is this value used herein in the analysis as the best indicator of emission bandwidth.

In solid state lasers, in order to generate high levels of total energy per pulse, the active material should possess a high value for laser figure-of-merit, FOM_(laser), defined by the following formula:

FOM_(Laser)=σ_(em)τ_(Rad)/(n ₂Δλ_(eff))

wherein

σ_(em) is the maximum emission cross section, [×10⁻²⁰ cm²],

τ_(Rad) is the radiative lifetime, (μsec);

n₂ is the nonlinear refractive index; and

Δλ_(eff) is the effective emission bandwidth, [nm].

This laser figure-of-merit has been developed in accordance with the invention to provide guidance in selecting glasses for use in high energy laser systems. Larger values of emission cross section provide higher laser gain for the same doping level, while larger values of radiative lifetime imply a higher amount of stored energy in the laser glass medium during pumping. Glasses with lower values of nonlinear index can support higher laser fluence values without the appearance of laser induced damage. Also, as discussed earlier, a narrow emission bandwidth is desirable as it provides a better overlap between the emitted light from the glass and the bandwidth of the actual laser system.

In accordance with another aspect of the invention, the aluminophosphate glass composition according to the invention possesses one or more of the following properties:

(1) a thermal-mechanical figure of merit, FOM_(TM), of at least 0.9 W/m^(1/2), preferably at least 1.1 W/m^(1/2), especially at least 1.2 W/m^(1/2), and in particular at least 1.3 W/m^(1/2), for example 0.9-1.8 W/m^(1/2);

(2) a maximum emission cross section, σ_(em), of at least 2.5×10⁻²⁰ cm², preferably at least 2.8×10⁻²⁰ cm², especially at least 3.0×10⁻²⁰ cm², and in particular at least 3.2×10⁻²⁰ cm², for example 2.5-4.5×10⁻²⁰ cm².

EXAMPLES

Examples All of the glasses are made using laser grade ingredients and melted under a dry oxygen environment with stirring, using a Pt stirrer for better homogeneity.

Tables 1A and 1B list Examples 1-15 of the glass composition according to the invention, as well as Comparative Examples A-F (which do not contain SiO₂ or B₂O₃). In Table 1A, the glasses of Examples 1-8 and Comparative Examples A-C contain appreciable amounts of Li₂O. In Table 1B, the glasses of Examples 9-15 and Comparative Examples D-F contain appreciable amounts of MgO.

To determine the emission spectrum, the glasses are cast into molds and appropriately annealed to remove stress. Nd-doped glasses are prepared as bulk cuvette samples at least nominally 10 mm×10 mm×40 mm in size. Cuvette samples of each Nd doped glass is used to measure an emission spectrum, from which the effective emission bandwidth (Δλ_(eff)) is determined according to Equation (1):

$\begin{matrix} {{\Delta \; \lambda_{eff}} = \frac{\int{{I(\lambda)}{\lambda}}}{I_{\max}}} & (1) \end{matrix}$

where the integrated area of the emission spectrum is made between 1000 nm to 1200 nm for Nd and the maximum emission intensity (I_(max)) is found at the wavelength close to 1055 nm for Nd.

Tables 2A and 2B summarize the optical, thermal, and physical properties of the glasses of Examples 1-15, in accordance with the invention, and Comparative Examples A-F. Table 2C summarize properties of commercial Nd-doped phosphate laser glasses APG-1 and APG-2, sold by Schott North America, Inc., as well as the glasses identified as APG-300 and APG-400. These latter two glasses correspond to test melts that have the same composition as the commercial glasses APG-1 and APG-2, but are substantial smaller in size (half liter versus 100 liter). Also, these melts are prepared using the same procedure used for making the tests melts of Examples 1-15 and A-F, rather than the full scale production used for making the commercial glasses APG-1 and APG-2. Thus, as can be seen in Table 2C, there are some differences between the properties of APG-300 and APG-400, in comparison to those of APG-1 and APG-2, respectively.

As can be seen from Table 2A, the thermal-mechanical figure of merit values, FOM_(TM), for Examples 1-8 are higher than those of Comparative Examples A-C. However, all of these glasses have lower thermal-mechanical figure of merit values than that of the APG-2 glass test melt, i.e., APG-400. As noted above of the two commercial glasses APG-1 and APG-2, the latter has the better thermal-mechanical properties.

As can be seen from Table 2A, the thermal-mechanical figure of merit values, FOM_(TM), for Examples 9-15 are higher than those of Comparative Example D and Comparative Examples F. However, the glasses of Examples 9, 10, and 14 showed lower thermal-mechanical figure of merit values than that of Comparative Example E. As shown in Table 3B, Comparative Example E exhibits a very low Laser figure of merit value.

Tables 3A and 3B summarize the laser properties of the glasses of Examples 1-15, in accordance with the invention, and Comparative Examples A-F. Table 3C summarizes the laser properties of APG-1, APG-2, APG-300 and APG-400.

As can be seen from Table 3A, the Laser figure of merit values, FOM_(Laser), for Examples 1-8 are higher than those of Comparative Example B and Comparative Example C. However, the glasses of Examples 5, 7, and 8 showed lower Laser figure of merit values than that of Comparative Example A. As shown in Table 2A, Comparative Example A exhibits a low thermal-mechanical figure of merit value.

Referring to Table 3B, the Laser figure of merit values, FOM_(Laser), for Examples 9-15 are higher than those of Comparative Example E, and only Example 12 has a lower Laser figure of merit value than those of Comparative Examples D and F. On the other hand, Example 12 exhibits a high thermal-mechanical figure of merit value.

The last line in Tables 2A and 2B provide a percentage comparison of the FOM_(TM) values of Examples 1-15 and Comparative Examples A-F with that of the APG-2 control melt, i.e., APG-400. The last line in Tables 3A and 313 provide a percentage comparison of the FOM_(Laser) values of Examples 1-15 and Comparative Examples A-F with that of the APG-1 control melt, i.e., APG-300. Adding these two percentages together for each of the glasses, one can see that the glasses of Examples 1-15 exhibit advantageous thermal-mechanical and laser properties, in comparison to the glasses that do not contain SiO₂ or B₂O₃, i.e. Comparative Examples A-F.

TABLE 1A Examples of P₂O₅—Al₂O₃—B₂O₃/SiO₂ Glass Compositions (mol %) with high Alkali Metal Content Metal Oxide EXAMPLES Content 1 2 3 4 5 6 7 8 A B C S_(i)O₂ 5.00 5.00 10.00 5.00 8.50 7.00 5.00 B₂O₃ 5.00 5.00 8.00 5.00 5.00 7.00 6.00 Al₂O₃ 6.83 8.83 9.83 8.83 10.83 10.83 7.83 8.83 6.83 6.83 5.83 P₂O₅ 61.27 61.27 61.27 61.27 61.27 61.27 61.27 64.27 61.27 61.27 61.27 Li₂O 24.59 17.59 14.59 10.78 8.78 11.78 9.59 9.78 24.59 24.59 20.59 MgO 5.00 TiO₂ 5.00 ZnO La₂O₃ 1.19 6.19 3.19 8.00 1.50 1.19 6.19 1.19 11.19 Nd₂O₃ 1.00 1.00 1.00 1.00 1.00 1.00 1.00 1.00 1.00 1.00 1.00 As₂O₃ 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 Total

TABLE 1B Examples of P₂O₅—Al₂O₃—B₂O₃/SiO₂ Glass Compositions (mol %) with high Alkaline Earth Metals Content Metal Oxide EXAMPLES Content 9 10 11 12 13 14 15 D E F S_(i)O₂ 5.00 4.00 5.00 8.00 3.00 B₂O₃ 5.00 5.00 5.00 4.00 7.00 Al₂O₃ 6.83 8.83 8.83 9.83 9.83 9.83 9.83 6.83 6.83 8.83 P₂O₅ 61.27 61.27 61.27 59.27 59.27 59.27 59.27 61.27 61.27 61.27 Li₂O 1.50 1.50 1.50 1.50 1.50 1.50 1.50 1.50 1.50 1.50 MgO 23.09 18.09 15.09 15.08 15.08 15.08 15.08 23.09 23.09 17.09 TiO₂ 5.00 ZnO 3.00 5.00 5.00 5.00 La₂O₃ 1.19 6.19 3.19 1.00 1.00 6.19 1.19 11.19 Nd₂O₃ 1.00 1.00 1.00 1.20 1.20 1.20 1.20 1.00 1.00 1.00 As₂O₃ 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 0.12 Total

TABLE 2A Optical, Thermal, and Physical Properties of Example Compositions Examples Optical/Thermal/Physical Property 1 2 3 4 5 Refractive Index at 587 nm @ 30° C./hr, n_(d) 1.53182 1.54850 1.53808 1.52524 1.54783 Abbe Number, V_(d) 67.67 65.30 67.08 68.07 64.83 Density, ρ [g/cm³] 2.588 2.806 2.692 2.554 2.847 Thermal Conductivity @ 25 C., K_(25° C.) [W/mK] 0.77 0.64 0.72 0.82 0.64 Thermal Conductivity @ 90 C., K_(90° C.) [W/mK] 0.86 0.95 0.84 0.95 0.76 Poisson Ratio, ν 0.25 0.25 0.24 0.22 0.24 Young's Modulus, E [GPa] 63.8 64.8 69.1 71.5 66.1 Linear Coef. of Thermal Expansion, 108.3 90.0 84.5 81.6 71.8 α_(20-300 C.) [10⁻⁷/K] Softening Point, T_(sp) [° C.] 547.5 590.4 630.9 689.2 662.7 Glass Transition Temperature, T_(g) [° C.] 449 485 504 539 538 Knoop Hardness, HK 427 423 496 554 465 α_(3.333 mm) [cm⁻¹] (A measure of residual OH content) 1.28 0.58 0.94 1.77 0.71 α_(3.0 mm) [cm⁻¹] (A measure of residual OH content) 0.64 0.35 0.49 0.89 0.39 FOM_(TM) = K_(90° C.)K_(IC) (1 − ν)/(αE) (W/m^(1/2)) 0.97 1.24 1.16 1.49 1.27 FOM_(TM) (Improvement from APG-2 Control Melt) −42% −27% −31% −12% −25% Examples Optical/Thermal/Physical Property 6 7 8 A B C Refractive Index at 587 nm @ 30° C./ 1.52997 1.52905 1.52599 1.55084 1.55869 1.57017 hr, n_(d) Abbe Number, V_(d) 68.77 68.28 68.79 64.35 50.54 62.90 Density, ρ [g/cm³] 2.626 2.614 2.567 2.805 2.616 3.004 Thermal Conductivity @ 25 C., 0.76 0.76 0.79 0.58 0.77 0.59 K_(25° C.) [W/mK] Thermal Conductivity @ 90 C., 0.88 0.89 0.92 0.64 0.83 0.68 K_(90° C.) [W/mK] Poisson Ratio, ν 0.23 0.23 0.22 0.26 0.25 0.26 Young's Modulus, E [GPa] 72.2 71.4 73.6 63.3 63.9 64.3 Linear Coef. of Thermal Expansion, 78.5 74.9 76.9 106.3 106.0 94.7 α_(20-300 C.) [10⁻⁷/K] Softening Point, T_(sp) [° C.] 668.4 672.0 674.7 547.4 561.9 570.4 Glass Transition Temperature, T_(g) [° C.] 535 533 537 460 456 478 Knoop Hardness, HK 473 475 518 404 413 382 α_(3.333 mm) [cm⁻¹] (A measure of residual 0.86 1.12 1.55 0.84 0.78 0.46 OH content) α_(3.0 mm) [cm⁻¹] (A measure of residual 0.43 0.55 0.87 0.52 0.42 0.31 OH content) FOM_(TM) = K_(90° C.)K_(IC) (1 − ν)/(αE) 1.27 1.35 1.14 0.56 0.80 0.59 (W/m^(1/2)) FOM_(TM) (Improvement from APG-2 −25% −20% −32% −67% −52% −65% Control Melt)

TABLE 2B Optical, Thermal, and Physical Properties of Further Example Compositions Optical/Thermal/ Examples Physical Property 9 10 11 12 13 14 15 D E F Refractive Index at 587 nm @ 1.51337 1.52475 1.52301 1.51254 1.51242 1.51627 1.51717 1.53896 1.54387 1.55308 30° C./hr, n_(d) Abbe Number, V_(d) 67.39 65.73 66.52 68.28 67.55 66.96 67.20 64.55 49.44 63.29 Density, ρ [g/cm³] 2.572 2.694 2.653 2.562 2.576 2.611 2.608 2.823 2.611 2.938 Indentation Fracture 0.90 1.00 0.87 1.00 0.82 0.60 Toughness for 3.0N Load, K_(IC [MPa · m) ^(1/2)] Indentation Fracture 0.98 1.15 0.96 0.95 Toughness for 9.8N Load, K_(IC [MPa · m) ^(1/2)] Thermal Conductivity @ 0.76 0.66 0.69 0.74 0.71 0.69 0.70 0.66 0.83 0.59 25° C., K_(25° C.) [W/mK] Thermal Conductivity @ 0.82 0.77 0.82 0.86 0.84 0.81 0.84 0.71 0.84 0.69 90° C., K_(90° C.) [W/mK] Poisson Ratio, ν 0.24 0.24 0.23 0.23 0.23 0.23 0.23 0.25 0.24 0.26 Young's Modulas, E [GPa] 64.5 62.6 65.2 66.3 64.7 63.7 64.6 62.0 64.3 62.6 Linear Coef. of Thermal 67.9 66.7 65.0 61.8 62.5 62.0 59.2 68.9 61.4 68.3 Expansion, α_(20-300 C.) [10⁻⁷/K] Softening Point, T_(sp) [° C.] 697.2 732.7 743.9 711.4 715.7 725.6 671.4 679.7 Glass Transition Temperature, 558 566 564 578 564 562 569 544 568 551 T_(g) [° C.] Knoop Hardness, HK 407 409 462 498 401 429 436 394 408 419 α_(3.333 mm) [cm⁻¹] (A measure 0.82 0.44 0.82 0.92 0.50 0.08 0.92 0.40 0.50 0.49 of residual OH content) α_(3.0 mm) [cm⁻¹] (A measure 0.41 0.26 0.42 0.49 0.29 0.43 0.44 0.24 0.30 0.35 of residual OH content) FOM_(TM) = K_(90° C.)K_(IC)(1 − ν)/ 1.29 1.37 1.70 1.62 1.53 1.37 1.68 1.02 1.54 0.71 (αE) (W/m^(1/2)) FOM_(TM) (Improvement from −24% −19% 1% −4% −9% −19% 0% −39% −9% −58% APG-2 Control Melt)

TABLE 2C Optical, Thermal, and Physical Properties of Comparison Glasses Glasses Optical/Thermal/Physical Property APG-1 APG-300 APG-2 APG-400 Refractive Index at 587 nm @ 30° C./hr, n_(d) 1.513 1.50900 Abbe Number, V_(d) 66.9 67.40 Density, ρ [g/cm³] 2.559 2.561 Indentation Fracture Toughness for 3.0N Load, K_(IC) [MPa · m^(1/2)] Indentation Fracture Toughness for 9.8N Load, K_(IC) 1.05 [MPa · m^(1/2)] Thermal Conductivity @ 25° C., K_(25°) _(C.) [W/mK] 0.78 0.79 0.80 0.76 Thermal Conductivity @ 90° C., K_(90°) _(C.) [W/mK] 0.83 0.86 0.84 0.83 Poisson Ratio, ν 0.24 0.25 0.23 0.24 Young's Modulas, E [GPa] 70 66.8 63.8 61.7 Linear Coef. of Thermal Expansion, α_(20-300 C) [10⁻⁷/K] 99.6 99.3 62.6 63.7 Softening Point, T_(sp) [° C.] 668.4 Glass Transition Temperature, T_(g) [° C.] 450 457 546 Knoop Hardness, HK 450 434 420 400 α_(3.333 mm) [cm⁻¹] (A measure of residual OH 1.28 0.47 content) α_(3.0) _(mm) [cm⁻¹] (A measure of residual OH content) 0.64 0.27 FOM_(TM) = K_(90°) _(C.)K_(IC)(1-ν)/(αE) (W/m^(1/2)) 0.84 1.69 FOM_(TM) (Improvement from APG-2 Control Melt) −50% 0%

TABLE 3A Laser Properties of Example Compositions according to the Invention Examples Laser Property 1 2 3 4 5 6 7 8 A B C Refractive Index 1.524 1.540 1.530 1.515 1.539 1.522 1.521 1.518 1.542 1.547 1.561 at 1054 nm, n_(1054 nm) Non-linear 1.11 1.23 1.15 1.07 1.24 1.08 1.09 1.07 1.27 1.86 1.39 Refractive Index, n₂ [10⁻¹³ esu] Fluorescence 350 360 365 352 366 376 359 355 354 315 342 Lifetime, τ [μsec] Input Nd₂O₃ 3.00 2.63 2.76 2.94 2.46 2.84 2.89 2.90 2.69 2.98 2.42 [wt %] Peak Emission 1053.6 1054.2 1053.6 1053.2 1055.0 1053.7 1052.7 1052.6 1054.3 1053.7 1054.3 Wavelength, λ_(Peak) [nm] Effective 27.3 27.3 30.3 25.5 29.8 28.5 34.4 26.6 28.8 26.4 29.8 Emission Bandwidth, Δλ_(eff) [nm] Maximum 3.89 3.54 3.14 4.31 2.83 3.43 2.96 3.96 3.39 4.22 3.12 Emission Cross Section, σ_(em) [×10⁻²⁰ cm²] FWHM Emission 22.6 23.5 24.1 24.0 24.9 24.0 23.3 22.8 23.6 23.1 24.3 Bandwidth, Δλ_(FWHM) [nm] Radiative 325 354 365 323 407 359 344 334 346 298 359 Lifetime, τ_(Rad) (μsec) Judd-Ofelt 4.36 4.64 4.91 5.90 5.18 5.39 5.67 5.75 4.10 4.74 4.21 Parameter, Ω₂ [10⁻²⁰ cm²] Judd-Ofelt 5.20 4.47 4.39 5.08 3.92 4.55 4.71 4.87 4.68 5.52 4.22 Parameter, Ω₄ [10⁻²⁰ cm²] Judd-Ofelt 5.75 5.25 5.22 6.11 4.56 5.38 5.65 5.86 5.23 5.88 4.97 Parameter, Ω₆ [10⁻²⁰ cm²] FOM_(Laser) = 41.67 37.23 32.93 50.95 30.97 40.10 27.24 46.73 32.09 25.54 26.99 σ_(em)τ_(Rad)/ (n₂Δλ_(eff)) (×10^(−n)) FOM_(Laser) 8% −3% −15% +32% −20% 4% −29% 21% −17% −34% −30% (Improvement from APG-1 Control Melt)

TABLE 3B Laser Properties of Further Example Compositions according to the Invention Examples Laser Property 9 10 11 12 13 14 15 D E F Refractive Index at 1054 nm, 1.505 1.516 1.515 1.505 1.505 1.508 1.509 1.530 1.532 1.544 n_(1054 nm) Non-linear Refractive Index, 1.06 1.14 1.11 1.03 1.05 1.08 1.07 1.22 1.84 1.31 n₂ [10⁻¹³ esu] Fluorescence Lifetime, τ 316 323 350 350 346 344 344 314 257 323 [μsec] Input Nd₂O₃ [wt %] 3.52 3.26 3.30 3.55 3.55 3.46 3.45 3.17 3.51 2.88 Peak Emission 1054.8 1054.5 1053.9 1054.2 1054.2 1053.6 1053.7 1055.8 1055.2 1056.0 Wavelength, λ_(Peak) [nm] Effective Emission 31.7 29.7 30.4 38.2 31.7 31.0 30.8 32.7 31.4 31.0 Bandwidth, Δλ_(eff) [nm] Maximum Emission 2.87 2.84 2.74 2.20 2.82 2.66 2.62 2.68 3.08 2.75 Cross Section, σ_(em) [×10⁻²⁰ cm²] FWHM Emission 26.3 25.8 26.1 27.0 26.1 25.4 25.7 26.1 26.9 26.4 Bandwidth, Δλ_(FWHM) [nm] Radiative Lifetime, τ_(Rad) 388 416 424 425 401 431 438 390 328 399 (μsec) Judd-Ofelt Parameter, Ω₂ 6.58 5.99 6.03 6.09 6.15 5.99 6.05 5.62 6.34 5.34 [10⁻²⁰ cm²] Judd-Ofelt Parameter, Ω₄ 4.60 4.04 3.97 4.04 4.27 3.95 3.91 4.34 6.11 4.02 [10⁻²⁰ cm²] Judd-Ofelt Parameter, Ω₆ 4.96 4.64 4.57 4.67 4.96 4.56 4.46 4.68 4.70 4.55 [10⁻²⁰ cm²] FOM_(Laser) = 33.28 35.03 34.42 23.72 34.02 34.34 34.69 26.26 17.46 27.05 σ_(em)τ_(Rad)/(n₂Δλ_(eff)) (×10^(−n)) FOM_(Laser) (Improvement −14% −9% −11% −38% −12% −11% −10% −32% −55% −30% from APG-1 Control Melt)

TABLE 3C Laser Properties of Nd-doped Phosphate Comparison Glasses Glasses Laser Property APG-1 APG-300 APG-2 APG-400 Refractive Index at 1054 nm, n₁₀₅₄ nm 1.526 1.525 1.530 1.532 Non-linear Refractive Index, n₂ [10⁻¹³ esu] 1.13 1.11 1.22 1.84 Fluorescence Lifetime, τ[μsec] 354 314 257 Input Nd₂O₃ [wt %] 2.96 3.17 3.51 Peak Emission Wavelength, λ_(Peak) [nm] 1053.9 1054.3 1055.8 1055.2 Effective Emission Bandwidth, Δλ_(eff) [nm] 27.8 28.4 32.7 31.4 Maximum Emission Cross Section, σ_(em) 3.35 3.68 2.68 3.08 [x10⁻²⁰ cm²] FWHM Emission Bandwidth, Δλ_(FWHM) [nm] 23.3 26.1 26.9 Radiative Lifetime, τ_(Rad) (μsec) 361 331 390 328 Judd-Ofelt Parameter, Ω₂ [10⁻²⁰ cm²] 4.43 5.62 6.34 Judd-Ofelt Parameter, Ω₄ [10⁻²⁰ cm²] 5.05 4.34 6.11 Judd-Ofelt Parameter, Ω₆ [10⁻²⁰ cm²] 5.68 4.68 4.70 FOM_(Laser) = σ_(em) τ_(Rad)/(n₂Δλ_(eff)) (x10^(−n)) 38.54 26.26 17.46 FOM_(Laser) (Improvement from APG-1 Control Melt) 0% −32% −55%

The entire disclosure[s] of all applications, patents and publications, cited herein, are incorporated by reference herein.

The preceding examples can be repeated with similar success by substituting the generically or specifically described reactants and/or operating conditions of this invention for those used in the preceding examples.

From the foregoing description, one skilled in the art can easily ascertain the essential characteristics of this invention and, without departing from the spirit and scope thereof, can make various changes and modifications of the invention to adapt it to various usages and conditions. 

1. An aluminophosphate glass composition comprising (based on mol %): SiO₂  0.00-12.00 B₂O₃  0.00-15.00 Al₂O₃  6.00-11.00 P₂O₅ 55.00-67.00 Li₂O  0.50-26.00 K₂O 0.00-4.00 Na₂O 0.00-4.00 Rb₂O 0.00-4.00 Cs₂O 0.00-4.00 MgO  0.00-25.00 ZnO 0.00-6.00 TiO₂ 0.00-6.00 La₂O₃  0.00-10.00 Nd₂O₃ 0.00-6.00 R₂O (R = Li, Na, K, Rb, Cs)  0.50-26.00 MO (M = Mg, Ca, Sr, Ba, Zn)   0.00-25.00.

wherein Ln₂O₃ (Ln=Nd, Yb, or other lasing rare earth ions) is >0.00-10.00 mol %; R₂O is 8.0-26.0 mol % and MO is 0.0-6.0 mol %, or R₂O is 0.5-8.0 mol % and MO is 6.0-25.0 mol %; the sum of SiO₂, B₂O₃, and Al₂O₃ is 6.0-28.0 mol %; and when R₂O is ≧16.0 mol %, then Al₂O₃ is 6.0-10.0 mol % and the sum of SiO₂, B₂O₃, and Al₂O₃ is 6.0-15.0 mol %.
 2. An aluminophosphate glass composition according to claim 1, wherein the sum of SiO₂ and B₂O₃ is 3-20 mol %.
 3. An aluminophosphate glass composition according to claim 1, wherein said glass composition comprises: 10.00 mol % S_(i)O₂ (±2.00 mol %), 8.00 mol % B₂O₃ (±2.00 mol %), 8.80 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 10.80 mol % Li₂O (±2.00 mol %), <1.0 mol % MgO, <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).
 4. An aluminophosphate glass composition according to claim 1, wherein said glass composition comprises: 8.50 mol % S_(i)O₂ (±2.00 mol %), 5.00 mol % B₂O₃ (±100 mol %), 10.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 12.00 mol % Li₂O (±2.00 mol %), <1.0 mol % MgO, <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).
 5. An aluminophosphate glass composition according to claim 1, wherein said glass composition comprises: 7.00 mol % S_(i)O₂ (A: 2.00 mol %), 7.00 mol % B₂O₃ (±2.00 mol %), 8.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 10.00 mol % Li₂O (±2.00 mol %), 5.00 mol % MgO (±1.00 mol %), <1.0 mol % La₂O₃, 0.1-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).
 6. An aluminophosphate glass composition according to claim 1, wherein said glass composition comprises: 4.00 mol % S_(i)O₂ (±2.00 mol %), 5.00 mol % B₂O₃ (±2.00 mol %), 9.00 mol % Al₂O₃ (±1.00 mol %), 61.20 mol % P₂O₅ (±3.50 mol %), 1.50 mol % Li₂O 2.00 mol %), 15.00 mol % MgO (±2.00 mol %), <1.0 mol % La₂O₃, 0.2-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).
 7. An aluminophosphate glass composition according to claim 1, wherein said glass composition comprises: <3.0 mol % S_(i)O₂, 7.00 mol % B₂O₃ (±2.00 mol 10.00 mol % Al₂O₃ (±1.00 mol %), 60.00 mol % P₂O₅ (±3.50 mol %), 1.50 mol % Li₂O (±2.00 mol %), 15.00 mol % MgO (±2.00 mol %), 5.00 mol % ZnO (±1.00 mol %), <1.0 mol % La₂O₃, 0.3-1.00 mol % Nd₂O₃ or Yb₂O₃ (±0.50 mol %), and 0.10 mol % As₂O₃ (±0.05 mol %).
 8. A glass composition according to claim 1, wherein said composition contains 7-26 mol % Li₂O, the sum of the amounts of SiO₂ and B₂O₃ is 3-20 mol %, and the sum of the amounts of SiO₂, B₂O₃, and Al₂O₃ is 10.0-28.0 mol %.
 9. A glass composition according to claim 1, wherein said composition contains 14-25 mol % MgO, the sum of the amounts of SiO₂ and B₂O₃ is 3-12 mol %, and the sum of the amounts of SiO₂, B₂O₃, and Al₂O₃ is 10.0-25.0 mol %.
 10. A glass composition according to claim 1, wherein said composition contains 8.0-26.0 mol % R₂O and 0.0-6.0 mol % MO.
 11. A glass composition according to claim 1, wherein said composition contains 0.5-3.0 mol % R₂O and 10.0-25.0 mol % MO.
 12. A glass composition according to claim 1, wherein said composition contains 57-65 mol % P₂O₅.
 13. A glass composition according to claim 1, wherein said composition contains 59-62 mol % P₂O₅.
 14. A glass composition according to claim 1, wherein said composition contains 3.0-10.0 mol % SiO₂.
 15. A glass composition according to claim 1, wherein said composition contains 3.0-9.0 mol % B₂O₃.
 16. A glass composition according to claim 1, wherein said composition contains 6.0-10.0 mol % Al₂O₃.
 17. A glass composition according to claim 1, wherein said composition contains 1.0-7.0 mol % La₂O₃.
 18. A glass composition according to claim 1, wherein the amount of ZnO is 0.0-6.0 mol %, and the amounts of CaO, SrO, and BaO are each 0.0-5.0 mol %.
 19. A glass composition according to claim 18, wherein the total combined amount of CaO, SrO, and BaO is 0.0-5.0 mol.
 20. A glass composition according to claim 1, wherein the total combined amount of Na₂O, K₂O, Rb₂O, and Cs₂O is 0.0-4.0 mol %.
 21. A glass composition according to claim 1, wherein the amount of TiO₂ is 0.0-1.0 mol %.
 22. A glass composition according to claim 1, wherein the thermal-mechanical figure of merit value, FOM_(TM), is at least 9.00.
 23. A glass composition according to claim 1, wherein the maximum emission cross section, σ_(em), is at least 2.5 cm².
 24. In a solid state laser system comprising a solid gain medium and a pumping source, the improvement wherein said solid gain medium is a glass having a composition according to claim
 1. 25. A method for generating a laser beam pulse comprising flashlamp pumping or diode pumping a glass composition according to claim
 1. 